EP0742288B1 - Acier pour roulements trempe par induction et longue duree de vie - Google Patents

Acier pour roulements trempe par induction et longue duree de vie Download PDF

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Publication number
EP0742288B1
EP0742288B1 EP95937176A EP95937176A EP0742288B1 EP 0742288 B1 EP0742288 B1 EP 0742288B1 EP 95937176 A EP95937176 A EP 95937176A EP 95937176 A EP95937176 A EP 95937176A EP 0742288 B1 EP0742288 B1 EP 0742288B1
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EP
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Prior art keywords
steel
total
induction
rolling fatigue
content
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Expired - Lifetime
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EP95937176A
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German (de)
English (en)
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EP0742288A1 (fr
EP0742288A4 (fr
Inventor
Tatsuro Ochi
Yuji Kawauchi
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Nippon Steel Corp
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Nippon Steel Corp
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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10S—TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10S148/00—Metal treatment
    • Y10S148/902—Metal treatment having portions of differing metallurgical properties or characteristics
    • Y10S148/906—Roller bearing element

Definitions

  • This invention relates to a long-lived induction-hardened bearing steel. More particularly, the present invention relates to a steel which is produced through a step of controlling oxide inclusions and a induction hardening step, and which will be suitable for bearing parts such as outer rings, inner rings, rollers, etc, used under high load conditions.
  • SUJ 2 As a kind of steel in this field, SUJ 2 (according to JIS), for example, has been widely used as a steel which has improved rolling fatigue life. Since the C and Cr contents are high in this steel kind, large eutectic carbides are formed, so that a long annealing time is necessary for these eutectic carbides.
  • Japanese Unexamined Patent Publication (Kokai) No. 55-145158 discloses a Te-containing bearing steel and Japanese Unexamined Patent Publication (Kokai) No. 1-255651 discloses a bearing steel to which REM is added.
  • REM Japanese Unexamined Patent Publication
  • the inventors of the present invention proposed in Japanese Patent Application No. 6-134535 a high carbon chromium type bearing steel containing suitable amounts of Mg and Mo. Excellent rolling fatigue characteristics can be obtained by using this steel.
  • a spheroidization annealing step and a hardening/tempering step are necessary, and the production cost becomes high. Therefore, the total production cost of the bearing parts using the Mg- and Mo-containing high carbon chromium type bearing steel involving the increase of the material cost becomes remarkably high. For this reason, there is also a strong requirement for low cost during the production of the bearing parts.
  • the inventors of the present invention have paid specific attention to induction hardening which will replace the hardening/temperating step of the conventional high carbon chromium type bearing steel, or a carburizing step of a medium carbon steel. Because great compression residul stress occurs in the surface layer of the induction hardened material, longer service life can be effectively obtained. To accomplish a induction hardened bearing steel capable of obtaining excellent rolling fatigue characteristics even under a high load, the present inventors have furthered their studies and have made the following observation.
  • the present invention has been completed on the basis of the novel finding described above, and its gist resides in the following points.
  • each of Claims 1 to 4 provides a long-lived induction-hardened bearing steel which comprises, in terms of weight: 0.45 to 0.70% of C, 0.05 to 1.70 of Si, 0.35 to 2.0% of Mn, 0.001 to 0.03% of S, 0.010 to 0.07% of Al, 0.003 to 0.015% of N, 0.0005 to 0.0300% of total Mg; or further 0.05 to 1.20% of Mo; or further, one or at least two elements selected from the group consisting of the following elements in the following amounts; 0.03 to 1.50% of Cr, 0.10 to 2.00% of Ni, 0.03 to 0.7% of V, 0.005 to 0.3% of Nb, 0.0005 to 0.005% of B; and further, not more than 0.025% of P, not more than 0.0040% of Ti, not more than 0.0020% total O, and the balance consisting of iron and unavoidable impurities.
  • the invention of Claim 5 relates to the long-lived induction-hardened bearing steel wherein oxides contained in the steel satisfy the following formula in terms of a number ratio: (number of MgO•Al 2 O 3 + number of MgO)/number of total oxide type inclusions ⁇ 0.80.
  • the present invention gives specific attention to induction hardening as a step which will replace hardening/tempering of a conventional high carbon chromium type bearing steel or a carburization step of a medium carbon steel in order to produce bearing parts at a low cost, and accomplishes a bearing steel. Since a large compression residual stress occurs in the surface layer of a induction-hardened material, it is effective for improving life and furthermore, excellent rolling fatigue characteristics can be obtained even under a high load condition.
  • Carbon is an effective element for obtaining a rolling fatigue strength and a wear resistance necessary for bearing parts as the final products.
  • the effect of C is not sufficient when its content is less than 0.45%, and when the content exceeds 0.70%, toughness is deteriorated and a deterioration of the strength occurs, on the contrary. Therefore, the C content is defined to be from 0.45 to 0.70%.
  • Silicon is added for the purpose of deoxidizing and extending the life of the final products by inhibiting the formation of the white structure and the carbide structure and by preventing hardness reduction in the process of rolling fatigue.
  • the effects become insufficient when the Si content is less than 0.05%.
  • the content exceeds 1.70%, such effects are saturated, and the toughness of the final products is rather deteriorated. Accordingly, the Si content is defined to be from 0.05 to 1.70%.
  • Manganese is an effective element for increasing the life of the final products through the improvement of induction hardenability. When its content is less than 0.35%, however, this effect is not sufficient and if it exceeds 2.0%, on the other hand, the effect are saturated and the deterioration of the toughness of the final products is invited. Therefore, the Mn content is limited to 0.35 to 2.0%.
  • Sulfur is present in the steel as MnS, and contributes to improve the machinability thereof and make the structure fine.
  • the S content is less than 0.001%, the effects are insufficient.
  • the effects are saturated, and the rolling fatigue characteristics are rather deteriorated, when the S content exceeds 0.03%.
  • the S content is defined to be from 0.001 to 0.03%.
  • Aluminum is added as an element for deoxidation and grain refining, the effects become insufficient when the Al content is less than 0.010%. On the other hand, the effects are saturated, and the toughness is rather deteriorated when the Al content exceeds 0.07%. Accordingly, the Al content is defined to be from 0.010 to 0.07%.
  • Nitrogen contributes to make austenite grains fine through the precipitation behavior of AlN.
  • the effects become insufficient when the N content is less than 0.003%.
  • the effects are saturated, and the toughness is rather deteriorated, when the N content exceeds 0.015%. Accordingly, the N content is defined to be from 0.003 to 0.015%.
  • Magnesium is a strong deoxidizing element and reacts with Al 2 O 3 in the steel. It is added in order to deprive Al 2 O 3 of O and to form MgO•Al 2 O 3 or MgO. Therefore, unless at least a predetermined amount of Mg is added in accordance with the Al 2 O 3 amount, that is, in accordance with T.O wt%, unreacted Al 2 O 3 undesirably remains. As a result of a series of experiments in this connection, it has been found out that remainder of unreacted Al 2 O 3 can be avoided and the oxides can be completely converted to MgO•Al 2 O 3 or MgO by limiting the total Mg wt% to at least 0.0005%.
  • the Mg content is limited to 0.0005 to 0.3000%.
  • total Mg content represents hereby the sum of the soluble Mg content in the steel, the Mg content that forms the oxides, and other Mg compounds (that are unavoidably formed).
  • Phosphorus causes grain boundary segregation and center-line segregation in the steel and results in the deterioration of the strength of the final products. Particularly when the P content exceeds 0.025%, the deterioration of the strength becomes remarkable. Therefore, 0.025% is set as the upper limit of P.
  • Titanium forms a hard precipitation TiN, which triggers the formation of the white structure and the carbide structure. In other words, it functions as the start point of rolling fatigue failure and results in the deterioration of rolling life of the final products. Particularly when the Ti content exceeds 0.0040%, the deterioration of life becomes remarkable. Therefore, 0.0040% is set as the upper limit of Ti.
  • the total O content is the sum of the content of O dissolved in the steel and the content of O forming oxides (mainly alumina) in the steel.
  • the total O content approximately agrees with the content of O forming the oxides. Accordingly, when the total O content is higher, the amount of Al 2 O 3 in the steel to be reformed is greater.
  • the limit of the total O content from which the effects of the present invention in the induction-hardened material can be expected has been investigated.
  • the steel according to Claim 2 contains Mo in order to prevent hardness reduction in the rolling fatigue process and to inhibit the formation of the white structure and carbide structure.
  • Mo is added to improve induction hardenability and to improve life of the final products by inhibiting the formation of the white structure and the carbide structure in the rolling fatigue process.
  • Mo content is less than 0.05%, however, this effect is not sufficient and when it exceeds 1.2%, on the other hand, the effect is saturated and rather invites the deterioration of the toughness of the final product. Therefore, the Mo content is limited to 0.05 to 1.20%.
  • At least one of Cr, Ni, V, Nb and B is added so as to improve induction hardenability, to prevent hardness reduction in the rolling fatigue process and to inhibit the formation of the white structure and the carbide structure.
  • oxide inclusions outside the range of the present invention that is, oxide inclusions other than MgO•Al 2 O 3 and MgO, exist due to an unavoidable mixture.
  • the amounts of these inclusions are set to less than 20% of the total in terms of the number ratio, fine dispersion of the oxide inclusions can be highly stabilized, and further improvements in the materials can be recognized. Therefore, the number ratio is limited to (number of MgO•Al 2 O 3 + number of MgO/number of total oxide type inclusions ⁇ 0.8.
  • the present invention in order to bring the number ratio of the oxide inclusions into the range of the present invention, it is an effective method to prevent mixture of oxides of an external system such as those from refractories, but the present invention does not particularly limit the production condition relating to this requirement.
  • the production method of the steel according to the present invention is not particularly limited.
  • melting of a base molten steel may be carried out by a blast furnace-converter method or an electric furnace method.
  • the method of adding the components to the mother molten steel is not particularly limited, either, and a metal containing each component to be added or its alloy may be added to the mother molten steel.
  • the method of addition too, may be an addition method utilizing natural dropping, a blowing method using an inert gas, a method which supplies an iron wire, into which an Mg source is filled, into the molten steel, and so forth.
  • the method of producing a steel ingot from the mother molten steel and rolling the steel ingot is not particularly limited, either.
  • the present invention is directed to the steel for the bearing parts produced by the induction-hardening process, the induction-hardening condition, the existence of tempering, the tempering condition when it is effected, etc, are not particularly limited.
  • Rolling fatigue life was evaluated by using a Mori thrust-type contact rolling fatigue tester (Herzian maximum contact stress of 540 kgf/mm 2 ) and a point contact type rolling fatigue tester (Herzian maximum contact stress of 600 kgf/mm 2 ) using cylindrical rolling fatigue testpieces.
  • L 10 life "the number of repetitions of stress till fatigue failure at a cumulative destruction probability of 10% obtained by plotting test results on a Weibull chart" is generally used as L 10 life.
  • L 10 life "the number of repetitions of stress till fatigue failure at a cumulative destruction probability of 10% obtained by plotting test results on a Weibull chart” is generally used as L 10 life.
  • Tables 3 and 4 a relative value of this L 10 life of each steel material, when L 10 life of Comparative Example No. 34 was set to 1, was also shown.
  • the steels of the present invention had more excellent fatigue characteristics than the Comparative steels. Further, the existence of the white structure and the carbide structure was examined in each testpiece after rolling fatigue of 10 8 times, and the result was also
  • Comparative Example 34 the ratio of the MgO type oxide was 0, and the size of the oxides was a maximum of 20 ⁇ m and was coarse.
  • Comparative Example 37 represented the material to which a suitable amount Mg was added to the components approximate to those of Comparative Example 34.
  • the ratio of the MgO type oxide became 0.76, and the size of the oxides was reduced to 7 ⁇ m maximum.
  • the rolling fatigue characteristics were less than 6 times in both the Mori thrust type contact rolling fatigue test and the point contact type rolling fatigue characteristics and were not sufficient. This was because the amount of addition of Si was lower than the range of the present invention in Comparative Example 37, and the white structure and the carbide structure were formed in the rolling fatigue process, though the quantity was slight.
  • Comparative Examples 35 and 36 represent the cases where the component system other than Mg was within the range of the present invention, but the amount of addition of Mg was smaller than the range of the present invention in Comparative Example 35 while it was greater in Comparative Example 36.
  • the ratio of the MgO type oxides was as low as 0.48, and the size of the oxides was as coarse as 14 ⁇ m maximum.
  • the ratio of MgO type oxides was high, but coarse MgO was formed due to the excessive addition of Mg, and the size of the oxides was also as coarse as 14 ⁇ m maximum.
  • the white structure and the carbide structure were formed, though limitedly, in the rolling fatigue process. As a result, the rolling fatigue characteristics of these Comparative Examples were less than 5 times in both the Mori thrust type contact rolling fatigue test and point contact type rolling fatigue test in comparison with Comparative Example 34, and the rolling fatigue characteristics were not sufficient.
  • the ratio of the MgO type oxides was at least 0.7, and the size of the oxides was as fine as 9 ⁇ m maximum. Furthermore, the formation of the white structure and the carbide structure was restricted by optimizing the Si content and others. Accordingly, in comparison with Comparative Example 34 of the prior art steel, the steels of the present invention had extremely excellent fatigue characteristics of about 6 to about 11 times in the Mori system thrust type contact rolling fatigue test and about 6 to about 15 times in the point contact type rolling fatigue test. Particularly, Example 5 of the present invention had extremely excellent rolling life of at least about 8 times in the Mori thrust type contact rolling fatigue test and at least about 9 times in the point contact type rolling fatigue test in comparison with the prior art steels.
  • the induction hardened bearing steel of the present invention can realize the formation of fine oxide inclusions, the inhibition of forming white structures and carbide structures and the prevention of hardness reduction. As a result, it has become possible to provide a bearing steel which may greatly improve, in bearing parts, the rolling fatigue life under a high load. Accordingly, the effects of the present invention in industry are extremely significant.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Rolling Contact Bearings (AREA)
  • Sliding-Contact Bearings (AREA)
  • Heat Treatment Of Articles (AREA)

Claims (5)

  1. Acier pour paliers trempé par induction ayant une longue durée de vie comprenant, en termes de pour-cents en poids :
    C : 0,45 à 0,70%,
    Si : 0,05 à 1,70%,
    Mn : 0,35 à 2,0%,
    S : 0,001 à 0,03%,
    Al : 0,010 à 0,07%,
    N: 0,003 à 0,015%,
    Mg total : 0,0005 à 0,0300%,
    P : pas plus de 0,025%,
    Ti : pas plus de 0,0040%,
    O total : pas plus de 0,0020%, et
       le reste étant constitué par le fer et des impuretés inévitables.
  2. Acier pour paliers trempé par induction ayant une longue durée de vie comprenant, en termes de pour-cents en poids :
    C : 0,45 à 0,70%,
    Si : 0,05 à 1,70%,
    Mn : 0,35 à 2,0%,
    Mo : 0,05 à 1,20%,
    S : 0,001 à 0,03%,
    Al : 0,010 à 0,07%,
    N: 0,003 à 0,015%,
    Mg total : 0,0005 à 0,0300%,
    P : pas plus de 0,025%,
    Ti : pas plus de 0,0040%,
    O total : pas plus de 0,0020%, et
       le reste étant constitué par le fer et des impuretés inévitables.
  3. Acier pour paliers trempé par induction ayant une longue durée de vie comprenant, en termes de pour-cents en poids :
    C : 0,45 à 0,70%,
    Si : 0,05 à 1,70%,
    Mn : 0,35 à 2,0%,
    S : 0,001 à 0,03%,
    Al : 0,010 à 0,07%,
    N: 0,003 à 0,015%,
    Mg total : 0,0005 à 0,0300%,
       Au moins un des éléments choisis dans la groupe constitué par :
    Cr : 0,03 à 1,50%,
    Ni : 0,10 à 2,00%,
    V : 0,03 à 0,7%,
    Nb : 0,005 à 0,3%,
    B : 0,0005 à 0,005%, et
    P : pas plus de 0,025%,
    Ti : pas plus de 0,0040%,
    O total : pas plus de 0,0020%, et
       le reste étant constitué par le fer et des impuretés inévitables.
  4. Acier pour paliers trempé par induction ayant une longue durée de vie comprenant, en termes de pour-cents en poids :
    C : 0,45 à 0,70%,
    Si : 0,05 à 1,70%,
    Mn : 0,35 à 2,0%,
    Mo : 0,05 à 1,20%,
    S : 0,001 à 0,03%,
    Al : 0,010 à 0,07%,
    N: 0,003 à 0,015%,
    Mg total : 0,0005 à 0,0300%,
       Au moins un des éléments choisis dans la groupe constitué par :
    Cr : 0,03 à 1,50%,
    Ni : 0,10 à 2,00%,
    V : 0,03 à 0,7%,
    Nb : 0,005 à 0,3%,
    B : 0,0005 à 0,0050 %, et
    P : pas plus de 0,025%,
    Ti : pas plus de 0,0040%,
    O total : pas plus de 0,0020%, et
       le reste étant constitué par le fer et des impuretés inévitables.
  5. Acier pour paliers trempé par induction ayant une longue durée de vie selon l'une quelconque des revendications 1 à 4, caractérisé en ce que les oxydes contenus dans letdit acier répondent à la formule suivante comme rapport en nombre: (nombre de MgO·Al2O3 + nombre de MgO/nombre total d'inclusions de type oxyde ≥ 0,80.
EP95937176A 1994-11-24 1995-11-24 Acier pour roulements trempe par induction et longue duree de vie Expired - Lifetime EP0742288B1 (fr)

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
JP289643/94 1994-11-24
JP28964394A JP3512873B2 (ja) 1994-11-24 1994-11-24 高寿命高周波焼入れ軸受鋼
JP28964394 1994-11-24
PCT/JP1995/002394 WO1996016195A1 (fr) 1994-11-24 1995-11-24 Acier pour roulements trempe par induction et longue duree de vie

Publications (3)

Publication Number Publication Date
EP0742288A1 EP0742288A1 (fr) 1996-11-13
EP0742288A4 EP0742288A4 (fr) 1998-04-01
EP0742288B1 true EP0742288B1 (fr) 2002-05-08

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EP95937176A Expired - Lifetime EP0742288B1 (fr) 1994-11-24 1995-11-24 Acier pour roulements trempe par induction et longue duree de vie

Country Status (8)

Country Link
US (1) US5725690A (fr)
EP (1) EP0742288B1 (fr)
JP (1) JP3512873B2 (fr)
KR (1) KR100208677B1 (fr)
CN (1) CN1061699C (fr)
CA (1) CA2181918C (fr)
DE (1) DE69526645T2 (fr)
WO (1) WO1996016195A1 (fr)

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CN104630618B (zh) * 2015-01-19 2017-04-12 宁波钢铁有限公司 一种家用园艺工具用钢55MnB及其制备方法
CN108929997B (zh) * 2017-05-26 2021-08-17 宝山钢铁股份有限公司 一种汽车轮毂用轴承钢及其制造方法
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CN112813361A (zh) * 2021-01-05 2021-05-18 南京钢铁股份有限公司 一种五金工具用钢及其制备方法

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JP2730745B2 (ja) * 1988-12-09 1998-03-25 山陽特殊製鋼株式会社 耐食転動部品用鋼および転動部品
JP2760001B2 (ja) * 1989-01-24 1998-05-28 大同特殊鋼株式会社 高速度工具鋼
JPH0678566A (ja) * 1992-08-25 1994-03-18 Kanagawa Kagaku Gijutsu Akad 静電アクチュエータ
JP2978038B2 (ja) * 1993-08-16 1999-11-15 新日本製鐵株式会社 酸化物系介在物超微細分散鋼
JP3556968B2 (ja) * 1994-06-16 2004-08-25 新日本製鐵株式会社 高炭素系高寿命軸受鋼

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Publication number Publication date
EP0742288A1 (fr) 1996-11-13
CA2181918A1 (fr) 1996-05-30
KR970700782A (ko) 1997-02-12
JP3512873B2 (ja) 2004-03-31
JPH08144014A (ja) 1996-06-04
DE69526645D1 (de) 2002-06-13
KR100208677B1 (ko) 1999-07-15
EP0742288A4 (fr) 1998-04-01
WO1996016195A1 (fr) 1996-05-30
CN1139458A (zh) 1997-01-01
CA2181918C (fr) 2000-04-04
DE69526645T2 (de) 2002-11-28
CN1061699C (zh) 2001-02-07
US5725690A (en) 1998-03-10

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